Magnetic recording disk and sputtering process and apparatus for producing same

ABSTRACT

A magnetic thin film recording disk includes a substrate of a hard electroless plated nickel surface that has been textured to encourage a circular anisotropic orientation of crystal growth during a pass-by sputtering in a continuous production line. A thin film chromium nucleating layer that is substantially free of any oxidation that would affect the recording properties is subsequently deposited, and then a thin film magnetic layer of a cobalt alloy, having a desired circular anisotropic crystal growth, is deposited through the sputtering process. The resulting magnetic thin film recording disk is then coated with a thin film of a carbon protective material.

This is a division of application Ser. No. 210,119, filed on June 22,1988, for a MAGNETIC RECORDING DISK AND SPUTTERING PROCESS AND APPARATUSFOR PRODUCING SAME, now U.S. Pat. No. 4,894,133, which is a continuationof application Ser. No. 926,676, filed on Nov. 3, 1986, now abandonedwhich is a divisional application of Ser. No. 796,768, filed on Nov. 12,1985, now U.S. Pat. No. 4,735,840.

1. Field of the Invention

This invention relates to an apparatus and a method of depositingmagnetic thin films used for the magnetic recording media in a massproduction, direct current sputtering process and an improved magneticrecording disk product thereby.

2. Description of the Prior Art

The magnetic films that have been used in recording disk and tapesystems have been usually particulate in nature, the magnetic particlesbeing embedded in a binder material and then applied to the substrate.Recently, sputtered and evaporated thin film media have beeninvestigated and utilized for commercial data storage systems. Theadvantages of thinness, low defect level, smoothness and high inductionare particularly adaptable to high recording densities at the desirablelow flying heights of the head pieces. To provide high density recordingit has been recognized that the thin films should exhibit highmagnetization, high coercivity, and a square hysteresis loop. Examplesof thin film material have included cobalt nickel thin films that havebeen deposited upon sublayer films of gold to epitaxially orientate the"C" axis of the cobalt/nickel in the plane of the film.

There have been other suggestions to evaporate cobalt films onto achromium sublayer to increase the coercivity of the cobalt film.Chromium/cobalt deposit film structures have also been suggested usingRF diode sputtering. The chromium layer serves as a nucleating layer toprovide nucleating centers around which a subsequent magnetic film maygrow. Thus, the layer of nucleating material serves to form smallagglomerations that are evenly dispersed over the surface of aninsulating substrate.

Substrates of glass or aluminum alloys have been suggested forsubsequently receiving sputtered deposited layers of chromium cobalt,such as set forth in the article "Sputtered Multi-Layer Films forDigital Magnetic Recording" by Maloney, IEEE Transactions on Magnetics,Volume MAG-15, 3, July 1979. Examples of cobalt nickel magnetic thinfilms are suggested in the article "Effect of Ion Bombardment DuringDeposition on Magnetic Film Properties" by L. F. Herte et al., Journalof the Vacuum Society Technology, Volume 18, No. 2, March 1981. Finally,the use of a protective layer of carbon in a cobalt chromium structureis suggested in "The Optimization of Sputtered Co-Cr Layered Medium forMaximum Aerial Density" by W. T. Maloney, IEEE Transaction MagneticsVolume Mag-17, No. 6, Nov. 1981. The prior art has recognized theimportance of reducing the head-gap, the flying height and the mediumthickness but to date has not suggested a realization of a low costcommercial process of producing improved magnetic film disks on aproduction basis to realize the theoretical advantages of certainresearch results. Thus, there :s still a need to improve both theapparatus and process of producing and the characteristics of thinmagnetic film disks for commercial utilization.

SUMMARY OF THE INVENTION

The present invention provides a continuous production from a directcurrent planar magnetron sputtering apparatus for the mass production ofmagnetic thin film memory disks, a process for using the same and aresulting improved magnetic thin film memory disk resulting from theprocess.

The apparatus includes a series of pressure reducing entry and exitlocks that are positioned before and respectively after a series of maincoating chambers. The main coating chambers employ planar magnetronsputtering sources located on either side of the travel path of the diskto be coated. A carrier is designed to position a plurality of disksubstrates in a vertical plane for movement through the substratetransport system. Prior to loading on the carrier member, the substratesare pretreated by an abrasion process to provide circumferentialtexturing, e.g. concentric grooves that enhance the magnetic orientationin the plane of the disk. The substrates are mounted on the verticalsubstrate carrier and then subsequently heated, for example, to atemperature of about 100° C. The carrier with the substrates passesthrough an entrance lock slit valve and the initial pressure is reducedfirst by a mechanical pump, then by a cryogenic pump. The carrier thenpasses into a subsequent preliminary coating chamber where a secondpumping system reduces the pressure to enable a sputtering operation.

An inert gas is utilized to provide the plasma gas and can be selectedfrom one of argon and krypton. A relatively high inert gas pressure ispurposely introduced into the main coating chambers to destroy anyanisotropy of coercivity that could occur resulting from the angle ofincidence of the sputtered material as the carrier with the substratedisk approaches and egresses from rectangular planar sputtering sources.The higher gas pressure increases the incidence of collisionalscattering. The substrate carrier enters the first coating chamber andpasses between a pair of elongated direct current planar magnetronsputtering sources positioned on either side of the path of travel ofthe substrate. These sources provide a nucleating layer on both sides ofthe disk substrate and the material can be selected from chromium ortitanium. The nucleating layer favors the epitaxial formation of thesubsequent magnetic thin film layer on top of the nucleating layer. Thesubstrate carrier then passes into a second coating chamber having asecond pair of elongated direct current planar magnetron sputteringsources of a magnetic layer material again on either side of the path oftravel of the substrate carrier. The magnetic layer can be cobalt orpreferably a cobalt alloy, such as cobalt/nickel. The substrate carrierthen passes into the final coating chamber past a third pair ofelongated direct current planar magnetron sources of a protectivecoating material that is positioned on either side of the path of travelof the sub-strate carrier. The protective coating material is sputteredon top of the thin magnetic film layer to improve both the wearcharacteristics and to protect against corrosion. Various forms ofprotective overcoatings can be utilized, the preferred form beingcarbon. The coated memory disk is then removed from the production linewithout affecting the sputtering operation pressure range through theegressing locks. The disks are then subsequently tested for qualitycontrol and are ready for shipping to a customer.

The improved memory disk of the present invention comprises a substratecoated with chromium with preferably a layer of cobalt/nickel as themagnetic layer sealed with a protective coating of carbon. As a resultof this circumferential texturing, a circular anisotropic crystal growthhas occurred during the sputtering with a circumferential alignment thatprovides an improved memory disk having a reduced amplitude modulation,an improved squareness of the hysteresis loop, e.g. lower switchingfield distribution and a high production relatively low cost productionsystem. As a result, a higher recording linear bit density due to thehigh coercivity and low switching field distribution can be experiencedwith the magnetic disk of the present invention.

The features of the present invention which are believed to be novel areset forth with particularity in the appended claims. The presentinvention, both as to its organization and manner of operation, togetherwith further objects and advantages thereof, may best be understood byreference of the following description, taken in conjunction with theaccompanying drawings.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a schematic illustration of a direct current planar magnetronsputtering process line;

FIG. 2 is a schematic perspective view of the production line;

FIG. 3 is a cross-sectional diagram of a magnetic film recording disk ofthe present invention;

FIG. 4 is a graph of a one revolution read/back voltage envelope showingamplitude modulation characteristics of a recording disk as a result ofsputtering at a low argon pressure;

FIG. 5 is a one revolution read back voltage envelope showing amplitudemodulation characteristics as a result of the sputtering process beingconducted in a high pressure argon gas;

FIG. 6 is a graph of amplitude modulation versus argon sputteringpressure;

FIG. 7 is a graph of switching field distribution versus argonsputtering pressure;

FIG. 8 is a graph of switching field distribution versus radialroughness;

FIG. 9 is a schematic illustration of process for applyingcircumferential texturing to a disk substrate;

FIG. 10 is a graph of coercivity versus thickness of the chromium layer;

FIG. 11 is a perspective view of a cobalt nickel crystal structure;

FIG. 12 is a perspective view of a chromium crystal structure, and

FIG. 13 is a combined graph of the hysteresis loop and the relationshipof switching field distribution.

DESCRIPTION OF THE PREFERRED EMBODIMENTS

The following description is provided to enable any person skilled inthe thin film deposition art to make and use the invention and setsforth the best modes contemplated by the inventor of carrying out hisinvention. Various modifications, however, will remain readily apparentto those skilled in these arts, since the generic principles of thepresent invention have been defined herein specifically to provide arelatively economical process for manufacturing thin film magnetic disksof an improved structure on a production basis. Referring to FIGS. 1 and2, a direct current planar magnetron sputtering production assembly line2 is shown and comprises from left to right a loading table 4 forreceiving a disk carrier 6, an entrance lock chamber 8 having an outerentrance lock 10 and an inner entrance lock 12.

The main deposition chamber 14 is subdivided into a preliminary chamber16 and sputtering chambers 18, 20 and 22, respectively. An exit chamber24 is the final chamber of the main deposition chamber 14 and ispositioned before the exit lock chamber 26. Finally, an unload table 28is provided along the production line.

As can be seen, the disk carrier 6, which is a flat multi-operationalmetal support plate, is transported through a series of rollers in auni-directional travel from the load table 4 to the unload table 28. Aninner lock valve 30 and an exit lock valve 32 are positioned on eitherside of the exit lock chamber 26. The main deposition chamber 14includes a series of partition walls having central apertures fordividing the respective sputtering chambers. A rotary mechanical pump(not shown) is used to lower the pressure in the entrance lock chamber 8to a pressure of about 0.5×10⁻² torr. Subsequently, a cryogenic pumpcontinues to lower the pressure to 2×10⁻⁵ torr, prior to the entrancelock chamber 8 being backfilled with relatively pure argon (99.99%) at apressure of 2×10⁻² torr. The entrance lock chamber pump 34 iscomplemented with a pair of main deposition chamber pumps 36 and 38.Finally, an exit lock chamber pump 40 is provided to evacuate the exitlock chamber 26.

The disk carrier 6 is particularly designed to be maintained in avertical plane as it passes through the main desposition chamber 14. Thefirst sputtering chamber 18 is provided with four direct current planarmagnetron sputtering sources 42 for providing a nucleating layer. Thesources 42 are approximately five inches wide by fifteen inches inlength and are approximately 3/8 of an inch thick with direct watercooling. The main deposition chamber 14 is also filled with argon at apressure of 2×10⁻² torr. This pressure range is relatively high for a DCplanar magnetron sputtering system since it is usually preferably tooperate at a much lower pressure to maximize the deposition rate of thetarget material. The use of the relatively high pressure of argon gasfor a DC planar magnetron sputtering procedure is specifically toprevent direct collision of the ions with the substrate disk at lowangles of incidence as the disk carrier 6 progressively moves throughthe assembly line 2. Usually the speed of the substrate transport systemfor the disk carrier 6 is a velocity within a range of 1 to 10 mm/sec,with a typical average speed of 3 mm/sec.

The next sputtering chamber 20 provides the magnetic layer and includestwo magnetron sputtering sources 44 positioned on either side of theline of travel of the disk carrier 6. The target dimensions areapproximately the same as the nucleating targets 42 and can, forexample, be cobalt/nickel alloy source 44. Finally, sputtering chamber22 includes a protective coating source 46, such as carbon, that againcomprises a pair of sources one on each side of the line of travel ofthe disk carrier 6. Each of the sources are essentially line sourceswith cosine distribution of their emission profile. The target spacingfor an opposing pair is 51/2 inches with a target to substrate spacingof approximately 21/2 inches preferred. The target source to substratedistance is preferably maintained within a range of 2 to 4 inches.

The direct current planar magnetron sources 42, 44 and 46 can use bothpermanent magnets or electro magnets for plasma confinement. Each sourceis independently powered by constant current 10 kw direct power supply.

Referring to FIG. 3, a substrate 50 can be selected from glass, anelectroless plated nickel over aluminum alloy 15 where the aluminumalloy is 5086, pure aluminum or a polycarbonate or a polyetheramideplastic. The substrate dimensions can be in the range of 95 mm to 230 mmin outer diameter with a thickness of 0.035 to 0.080 inches. Thearithmetic average of the substrate smoothness should be about 75 to 100angstroms. The nuclearing layer 52 can be selected from chromium andtitanium. Preferably, chromium is selected in the preferred embodiment.

As shown in FIG. 12, the chromium underlayer 52 provides a BCC (bodycentered cubic) structure with a (110) orientation of itscrystalographic plane parallel to the plane of the substrate disk 50.This (110) orientation provides the appropriate lattice parameter toinitiate the epitaxial growth in the magnetic thin film layer of a HCP(hexagonal close packed) phase with a (101 0) orientation that is the"C" axis is parallel to the substrate 50. Reference can be had to FIG.11 to show such an orientation of a cobalt/ nickel alloy. As can beappreciated by these skilled in this field, it is highly desirable tohave the hexagonal close pack phase (HCP) of the magnetic thin filmlayer orientated parallel to the plane of the disk for longitudinalrecording. Generally, the depositing of the magnetic film material, suchas the cobalt/nickel film, directly on a glass or aluminum substratewill obtain a FCC (Face Center Cubic) structure. However, the use of anucleating layer will provide the preferred orientation.

The thickness of the nucleating layer of chromium is within a range of1000 to 5000 angstroms. A preferred thickness for the nucleating layercan be approximately 3000 angstroms of chromium. The magnetic layer 54can be selected from one of cobalt, a cobalt/nickel alloy, acobalt/chromium alloy and a cobalt/vanadium alloy. In the cobalt/nickelalloys a range of 0 to 35% nickel and 65% to 100% cobalt could beutilized while in the cobalt/chromium alloys a range of 5 to 25%chromium could be utilized, and in the cobalt/vanadium alloys a 5 to 25%range of vanadium could be utilized. The thickness of the magnetic layeris approximately 200 to 1200 angstroms and is preferably in the range ofapproximate 750 angstroms.

Finally, a protective overcoat 56 is provided for wear resistance andcorrosion resistance. It is believed that titanium carbide, Boroncarbide and tungsten carbide could be utilized. The preferred protectiveovercoating is carbon having a layer thickness in the range of 200 to800 angstroms with 300 angstroms being an approximate preferred coatingthickness.

To achieve a high volume production with a continuous on-line sputteringprocess, disk carriers 6 are progressively moved through apertures ineach of the sputtering chambers 18, 20 and 22. The purpose of providinga nucleating layer 52 is to permit a "C" axis texture to be formed inthe subsequent magnetic layer 54 in a random manner. A problem hasoccurred, however, in that an anisotropic "C" axis texture is promotedby an early arrival of chromium atoms as the substrate enters throughthe aperture of the chamber 18 and the very large angle of incidenceresulting from the movement of the substrates during the constantsputtering process. This anisotropy of the "C" axis causes an anisotropyof coercivity which will produce a severe once around amplitudemodulation in an output signal recorded on the magnetic layer 52. Thisis a particularly objectionable property for a high density longitudinalrecording. This problem is graphically disclosed in FIG. 4 wherein aplus or minus 25% amplitude modulation has been experienced.

The present invention by providing a relatively high argon pressurerelative to a direct current planar magnetron sputtering process,removes this problem of anisotropic orientation by providing a randomdistribution of the sputtered atoms (presumably resulting from acollisional phenomena with the argon atoms at the relatively highpressure). Referring specifically to FIG. 6, the relationship betweenthe amplitude modulation of the read/back voltage and the argonsputtering pressure is graphically disclosed. As can be seen from thisgraph, higher pressure reduced the modulation while lower pressureswould increase the modulation.

Referring to FIG. 7, the relationship to switching field distribution(SFD) is disclosed for the magnetic layer as it varies with the argonsputtering pressures. The SFD ar lower pressures is correspondingly low,and at the higher pressures the SFD value is high. It is believed thatthis occurs because the larger and more uniform grain size is promotedat lower pressures and more variant grain sizes are promoted at higherpressures.

A lower SFD value, typically below 0.20 is particularly advantageous forhigh density magnetic recording since such values allow a highresolution of the recording bit transitions. By comparing FIGS. 6 and 7,it can be seen that the low argon pressures have an advantage withregard to the SFD value but provide a disadvantage with regard toamplitude modulation. Thus, a design factor in the present invention isa compromise in providing an argon pressure such as a range of 2.0 to4.0×10-2 torr. In operation, the present invention could utilize aplasma gas pressure range from 1×10⁻² torr. Operation below 1×10⁻² torrcan increase the amplitude modulation by a +15% operation above 7.5×10⁻²torr permits the columnar structure of the thin film to become tooporous and rough for permitting the recording head to fly close to thedisk surface. As those skilled in the art know, the closer the recordinghead can fly to the recording disk, the more efficient will be the readand write recording. Recording heads typically fly above the surface ofthe disk, supported by an air cushion at a distance of 6 to 12 microinches. Irregularities on the surface of the recording disk that couldinterfere or contact the recording head must be avoided.

FIG. 4 and FIG. 5 are representations of oscilloscope voltage traces forone revolution of travel around a disk circumference while sending theread/back signal from a high frequency 2 F MFM written pattern. FIG. 4shows the read/back voltage modulated by +25% which is an unacceptablevalue for present day magnetic recording read/write channels.

FIG. 5 shows the read/back voltage modulated by +5% which is a valuenecessary for the highest performance from a magnetic recording diskdevice.

The read/back signal amplitude modulation shown in FIG. 4 is caused byanisotropic orientation of the HCP "C" axis of the cobalt/nickel layershown in FIG. 11. This anisotropic orientation is in the plane of thedisk parallel to the direction of traverse passing the sputteringsources due to the sputtering of all layers at lower pressures(typically below 2.0×10⁻² torr) and consequently inducing a low angle ofincidence columnar film growth in preference to the direction of thesubstrate as it passes the sources.

This HCP "C" axis anisotropy causes the resulting film coercivity tohave a similar directional anisotropy and consequently causes variationsin the read/back signal voltage at varying circumferential positions asthe head travels around the disk in one revolution.

FIG. 5 shows a reduced modulation amplitude of the read/back voltagesignal due to a sputtering operation at higher pressures (typically2.0×10⁻² to 4.0×10⁻² torr).

Sputtering at these higher pressures causes collisional scattering ofsputtered atoms before they reach the substrate and hence a more randomfilm structure, which includes the random orientation of the HCP "C"axis of the cobalt/nickel layer in the plane of the disk, therebyeliminating any low angle of incident effects.

To improve the magnetic recording density, it is important to provide arelatively high squareness to the hysteresis loop as disclosed in FIG.13. The randomizing of the "C" axis by the increased gas pressure of thepresent invention lowers the amplitude modulation but only provides amodest squareness to the hysteresis loop.

The present invention has discovered that circumferential texturing orabrading of the disk surface can cause the "C" axis to orientate in acircumferential direction and thereby supply a more intense uniformcontinuous read/back signal to the flying head with a resulting verysquare hysteresis loop. Thus, a preliminary abrading of the substrate asshown in FIG. 9 is an advantage of the present invention. As mentionedearlier, one of the design goals in this art is to permit the recordinghead to fly as close as possible to the surface of the recording disk.The abrading step on the substrate would appear to be contrary to thisteaching. In fact, excessive roughness to the substrate will provide alimitation to the closeness by which the head can fly to the finishedrecording disk.

In FIG. 9, a substrate 58, such as a nickel plated aluminum member ispositioned on a rotating shaft 60 and rotated at a speed less than 200rpm. A diamond impregnated polyester tape 62 is applied to both sides ofthe disk substrate 58 to abrasively remove the nickel plating from thesubstrate in the shape of concentric grooves 66 roughly proportional tothe size of the diamond abrasive in the tape. Generally, the particlesize of the abrasive is typically in the range of 0.1 to 1.0 microns.This circumferential texturing can be accomplished by rotating thesubstrate 58 while pressing the diamond impregnated polyester tape 62against both sides of the disk in the presence of a fluid coolant, likekerosene, supplied through a nozzle 64. The coolant not only controlsthe temperature of the abrading process but also acts to remove anymicroscopic abraded debris.

Referring to FIG. 8, the relationship between the switching fielddistribution (SFD) and the radial roughness of the finished disk due tocircumferential texturing is disclosed. As the disk surface radialroughness increases due to a deliberate circumferential grooving the SFDdecreases. A low SFD is a desirable parameter for high densityrecording. It is believed that the physical cause of this effect is thepreferential orientation of the "C"--axis of the HCP phase of, forexample, a cobalt/nickel magnetic layer along a circumferential texturalline. It is also believed that this occurs primarily due to anyshadowing effects of the hills and valleys of the texturing. Theroughness factor should be in the range of 50 to 500 angstroms. Aroughness factor below 50 angstroms promotes higher switching fielddistribution and permits a more random "C" axis orientation. A roughnessor hill-to-valley distance above 500 angstroms can interfere with thefly characteristics of the recording head.

Referring again to FIGS. 1 and 2, a substrate disk, such as anelectroless plated nickel over aluminum alloy, with the aluminum alloybeing 5086 can be circumferentially textured as shown in FIG. 9 to aradial roughness factor of 200 angstroms prior to being loaded on to thedisk carrier 6. Usually, the substrates are preparatorily cleaned withdeionized water, a detergent of a non-ionic surfactant and ultrasonics(10 to 60 kilohertz). The substrates can also be inserted into a vaporphase of a trichlorotrifluoroethane vapor dryer. The substrate can alsobe preliminarily heated to 100 degrees Centrigrade as an additionalpreparatory step.

The cleaned and heated substrate can then be loaded onto disk carrier 6which then subsequently enters the entrance lock chamber 8, and when theouter door is closed the entrance lock chamber can be evacuated by arotary mechanical pump and then subsequently by a cryogenic pump 34. Thelock chamber 8 is filled with argon gas at a pressure of 2×10⁻² torr.The main deposition chamber 14 has been previously evacuated and pumpedto a base pressure of 2×10⁻⁷ torr as a result of the two cryogenic pumps36 and 38. This chamber is also filled with argon gas at a pressure of2×10⁻² torr. The disk carrier 6 then moves at a constant velocitythrough the respective sputtering chambers 18 through 22. Power issupplied to all of the sputtering sources, as more particularly seen inFIG. 2 and a plasma is initiated over each source to commence thesputtering. The entrance lock inner door or valve 12 opens and thevertically orientated disk carrier 6 moves forward at a speed ofapproximately 3 mm/sec. 3 kw of power are supplied to each of the fourchromium sources 42 which are utilized for the nucleating layer 52 asshown in FIG. 3. 2.5 kw of power is supplied to each of the twocobalt/nickel layer sources and 2.5 kw is supplied to each of the twocarbon protective layer sources. As the disk carrier 6 traverses pasteach of the deposition sources, they are uniformly coated, first with anucleating layer 52, then the magnetic layer 54 and finally theprotective layer 56. The actual substrate temperature willadvantageously be maintained by a heater 15 in a temperature range of 75degrees Centigrade to 250 degrees Centigrade. A temperature below 75degrees Centigrade will not permit a reliable adhesion of the thin filmlayers while a temperature above 250 degrees Centigrade can create awarp in the substrate disk and can cause the nickel phosphorous layer tobecome magnetic. It is believed that this may be caused by the migrationof the phosphorous to the grain boundaries at the higher temperature.

The actual thickness layer of the nucleating layer of chromium is withinthe range of 1000 to 5000 angstroms, and FIG. 9 discloses a graph ofcoercivity versus the chromium layer thickness. This graph was derivedfor a cobalt/nickel 80:20 alloy thickness with an argon pressure of2×10⁻² torr and a substrate temperature of 200 degrees Centigrade. Ascan be seen, for a given cobalt/nickel layer thickness coercivityincreases with increasing chromium thickness and for a given chromiumthickness coercivity decreases with an increasing cobalt/nickelthickness.

A magnetic layer, such as a cobalt/nickel alloy is deposited within therange of 200 to 1500 angstroms, and finally a protective coating, suchas carbon, is deposited within the range of 200 to 800 angstroms. Thedisk carrier then transports the finished coated magnetic recording diskto the exit lock chamber 26 which has been previously evacuated andpumped to 2×10⁻⁵ torr and then back filled with argon to 2 ×10⁻² torr.The interlock valve 30 is closed and the exit lock 32 is vented toatmospheric pressure with argon in less than 20 seconds. The diskcarrier 6 exits the exit lock 32 and the finished recording disks areunloaded for quality control testing. The empty disk carriers 6 arereturned for reloading for a subsequent production cycle.

Referring to FIG. 13, the switching field distribution (SFD) defines ameasure of the change in the drive field requirements to switch themagnetic domains of the magnetic layer. Graphically, this parameter isdefined by means of an unintegrated differential curve. By constructinga horizontal line at a vertical coordinate of one half the peak value,two points of the intersection result are defined as the horizontaldistance between these points. Delta H is defined as the horizontaldistance between these points. SFD is defined as divided by thecoercivity Hc. Hc is shown as the width of the hysteresis loop shown atthe bottom of the graph of FIG. 13.

While the above features of the present invention teach apparatus,process and an improved magnetic recording disk, it can be readilyappreciated that it would be possible to deviate from the aboveembodiments of the present invention and, as will be readily understoodby those skilled in the art, the invention is capable of manymodifications and improvements within the scope and spirit thereof.Accordingly, it will be understood that the invention is not to belimited by the specific embodiments but only by the spirit and scope ofthe appended claims.

I claim:
 1. A magnetic thin film recording disk comprising:a substratehaving an electroless plated nickel surface layer, the substrateincluding aluminum, the substrate characterized by a physically abradedsurface having a series of physical circumferential texturing of hillsand valleys prior to any sputtering operation to encourage a circularanisotropic orientation of crystal growth during sputtering, thehill-to-valley distance being within the range of 50 to 500 Angstroms; athin film chromium nucleating layer having a body centered cubicstructure with a (110) orientation of its crystalographic plane parallelto a plane of the substrate; a thin film magnetic layer of a cobaltalloy disposed on the nucleating layer with an epitaxial growth of ahexagonal close packed phase with a C axis parallel to the plane of thesubstrate, and a thin film carbon protective film disposed on themagnetic layer.
 2. The recording disk of claim 1 wherein a magneticswitching field distribution is less than 0.20.
 3. The recording disk ofclaim 1 wherein the substrate is a 5086 aluminum alloy.
 4. The recordingdisk of claim 1 wherein the cobalt alloy layer has a (1010) phaseorientation.
 5. The recording disk of claim 1 wherein the hill-to-valleydistance is less than 500 Angstroms.
 6. The recording disk of claim 1wherein the hill-to-valley distance is approximately 200 Angstroms orless.
 7. The recording disk of claim 6 wherein the chromium nucleatinglayer is substantially free of any oxidation that would effect therecording properties.
 8. The recording disk of claim 1 wherein thecarbon layer is within 200 to 800 Angstroms in thickness.
 9. Therecording disk of claim 1 wherein the thickness of the magnetic layer isapproximately 750 Angstroms.
 10. A magnetic thin film recording diskcomprising:a polycarbonate substrate having an arithmetic smoothness ofapproximately 75 to 100 Angstroms, the substrate having circumferentialfeatures of hill-to-valley sizes of 50 to 500 Angstroms; a firstmetallic nucleating layer over the polycarbonate substrate; a secondcoating layer over the first coating layer, the second coating layerforming a thin film magnetic layer of a cobalt alloy, and a thirdcoating layer over the second coating layer.
 11. The recording disk ofclaim 10 wherein a magnetic switching field distribution is less than0.20.
 12. The recording disk of claim 10 wherein the cobalt alloy layerhas a (1010) phase orientation.
 13. The recording disk of claim 12wherein the hill-to-valley distance is less than 500 Angstroms.
 14. Therecording disk of claim 12 wherein the hill-to-valley distance isapproximately 200 Angstroms.
 15. The recording disk of claim 12 whereinthe carbon layer is within 200 to 800 Angstroms in thickness.
 16. Therecording disk of claim 15 wherein the thickness of the magnetic layeris approximately 750 Angstroms.
 17. A magnetic thin film recording diskcomprising:a substrate including a glass material, the substratecharacterized by a surface having circumferential texturing of hills andvalleys prior to any sputtering operation to encourage a circularanisotropic orientation of crystal growth during sputtering, thehill-to-valley distance being within the range of 50 to 500 Angstroms; athin film chromium nucleating layer deposited on the substrate surfacehaving a body centered cubic structure with a (110) orientation of itscrystalographic plane parallel to a plane of the substrate; a thin filmmagnetic layer of a cobalt alloy disposed on the nucleating layer withan epitaxial growth of a hexagonal close packed phase with a C axisparallel to the plane of the substrate and a (1010) phase orientation,and a thin film carbon protective film disposed on the magnetic layer.18. The recording disk of claim 17 wherein the hill-to-valley distanceis 200 Angstroms or less.
 19. The recording disk of claim 17 wherein amagnetic switching field distribution is less than 0.20.
 20. Therecording disk of claim 17 wherein the hill-to-valley distance isapproximately 200 Angstroms.
 21. The recording disk of claim 20 whereinthe carbon layer is within 200 to 800 Angstroms in thickness.
 22. Therecording disk of claim 21 wherein the thickness of the magnetic layeris approximately 750 Angstroms.
 23. A magnetic thin film recording diskcomprising:a substrate having an electroless plated nickel surfacelayer, the substrate including aluminum, the substrate characterized bya physically abraded surface having a series of physical circumferentialtexturing of hills and valleys prior to any sputtering operation toencourage a circular anisotropic orientation of crystal growth duringsputtering, the hill-to-valley distance being within the range of 50 to500 Angstrom; a thin film chromium nucleating layer having a bodycentered cubic structure with a (110) orientation of its crystalographicplane parallel to a plane of the substrate; a thin film magnetic layerof a cobalt alloy disposed on the nucleating layer with an epitaxialgrowth of a hexagonal close packed phase with a C axis parallel to theplane of the substrate, and with a cobalt concentration greater than 65wt. %; and a thin film carbon protective film disposed on the magneticlayer.
 24. A magnetic thin film recording disk comprising:a substratehaving an electroless plated nickel surface layer, the substrateincluding aluminum, the substrate characterized by a physically abradedsurface having a series of physical circumferential texturing of hillsand valleys prior to any sputtering operation to encourage a circularanisotropic orientation of crystal growth during sputtering, thehill-to-valley distance being 200 Angstroms or less; a thin filmchromium nucleating layer having a body centered cubic structure with a(110) orientation of its crystalographic plane parallel to a plane ofthe substrate, the chromium film layer being substantially free of anyoxidation that would affect the recording properties; a thin filmmagnetic layer of a cobalt alloy disposed on the nucleating layer withan epitaxial growth of a hexagonal close packed phase with a C axisparallel to the plane of the substrate, and with a cobalt concentrationgreater than 65 wt. %; and a thin film carbon protective film disposedon the magnetic layer.